Process for passivating dielectric films

ABSTRACT

Methods are disclosed herein for depositing a passivation layer comprising fluorine over a dielectric material that is sensitive to chlorine, bromine, and iodine. The passivation layer can protect the sensitive dielectric layer thereby enabling deposition using precursors comprising chlorine, bromine, and iodine over the passivation layer.

REFERENCE TO RELATED APPLICATIONS

The present application is the U.S. National Phase of International Application PCT/US2010/052741 filed Oct. 14, 2010 and claims priority under 35 U.S.C. § 119(e) to U.S. Provisional Application No. 61/253,444 filed Oct. 20, 2009, both of which are hereby incorporated by reference in their entirety.

BACKGROUND

Field of the Invention

The application relates to passivation of ultra-high k films. In particular, the present invention concerns novel processes for depositing electrodes on top of ultra high-k films.

Description of Related Art

Atomic layer deposition (ALD) is generally a self-limiting process, whereby alternated pulses of reaction precursors saturate a substrate surface and leave no more than one monolayer of material per pulse. The deposition conditions and precursors are selected to generally provide self-saturating reactions, such that an adsorbed layer in one pulse leaves a surface termination that is non-reactive with the gas phase reactants of the same pulse. A subsequent pulse of different reactants reacts with the previous termination to enable continued deposition. Thus, each cycle of alternated pulses typically leaves no more than about one molecular layer of the desired material. The principles of ALD type processes have been presented by T. Suntola, e.g. in the Handbook of Crystal Growth 3, Thin Films and Epitaxy, Part B: Growth Mechanisms and Dynamics, Chapter 14, Atomic Layer Epitaxy, pp. 601-663, Elsevier Science B.V. 1994, the disclosure of which is incorporated herein by reference.

SUMMARY OF THE INVENTION

In accordance with one aspect, processes for passivating a high-k layer on a substrate in a reaction chamber are provided. In some embodiments, the processes include: providing a substrate with a high-k layer in a reaction chamber, wherein the high-k layer comprises a material that is sensitive to reaction with compounds comprising chlorine, bromine or iodine; and providing a fluorine containing chemical into the reaction chamber in a vapor phase, such that the fluorine containing chemical reacts with the high-k layer to form a passivation layer.

In accordance with another aspect, processes for forming a passivation layer film for a high-k layer on a substrate in a reaction chamber are provided. In some embodiments, the processes include providing a substrate with a high-k material, wherein the high-k layer comprises Sr or Ba and contacting the high-k material with a vapor phase pulse of a fluorine containing chemical.

In accordance with another aspect, processes for forming a titanium nitride containing thin film on a substrate in a reaction chamber comprising a plurality of titanium nitride deposition cycles are provided. In some embodiments, the deposition cycles include: providing a pulse of titanium fluoride into the reaction chamber in a vapor phase to form no more than about a single molecular layer of the titanium fluoride on the substrate; removing excess titanium fluoride from the reaction chamber; providing a pulse of a nitrogen containing vapor phase reactant to the reaction chamber such that the nitrogen containing vapor phase reactant reacts with the titanium fluoride on the substrate to form a titanium nitride containing thin film; and removing excess nitrogen containing vapor phase reactant and reaction byproducts, if any, from the reaction chamber.

In accordance with another aspect, processes for chemical vapor deposition (CVD) processes for forming a titanium nitride containing thin film on a substrate in a reaction chamber are provided. In some embodiments, the deposition cycles include: providing a substrate with a high-k layer in a reaction chamber, wherein the high-k layer comprises a material that is sensitive to reaction with compounds comprising chlorine; providing vapor phase titanium fluoride to the reaction chamber; providing vapor phase reactant comprising nitrogen to the reaction chamber such that the nitrogen containing vapor phase reactant reacts with the titanium fluoride to form a thin film comprising titanium nitride.

In accordance with another aspect, a capacitor structure is provided. In some embodiments, the capacitor structure includes an electrically conductive bottom electrode layer; a high k dielectric layer comprising Sr or Ba; a passivation layer directly on top of the high k dielectric layer comprising fluorine; and an electrically conductive top electrode layer.

BRIEF DESCRIPTION OF THE DRAWINGS

FIGS. 1a-1c . Photographs of the TiN/SrTiO₃/Si MIS structures when different numbers of cycles of TiF₄+NH₃ chemistry were used at the TiN/SrTiO₃ interface and TiCl₄+NH₃ was used for the bulk TiN electrode deposition. The different colors of the wafers are caused by the different thicknesses of the underlying SrTiO₃ layers, (b) 30 nm, and (c) 50 nm.

FIG. 2. Sheet resistance measurements of the Si/ALD-SrTiO₃/30 nm/ALD-TiN wafers after deposition of ALD TiN with two phase processes.

FIGS. 3a and 3b . Appearance of the wafers after fluorination of the surface with WF₆ prior to TiN deposition. Sheet resistance ˜350Ω/□(Ω/square) with a WF₆ pulse.

FIG. 4. Photograph of the wafer after depositing 500 cycles of TiN from TiF₄+NH₃ on SrTiO₃. The average sheet resistance was 483.00 Ω/□.

FIG. 5. Process flow for deposition of capacitor stack in accordance with one embodiment.

FIG. 6. Schematic diagram of a capacitor stack having a fluoride interfacial layer between a high-k layer and a top electrode layer in accordance with one embodiment.

FIG. 7. Schematic diagram of a capacitor stack having a fluoride interfacial layer between the bottom electrode and high-k layer in accordance with one embodiment.

FIG. 8. Schematic of a capacitor stack having a fluoride interfacial layers between the bottom electrode and high-k layer and top electrode and high-k layer in accordance with one embodiment.

FIG. 9. Schematic of a capacitor stack having a fluoride interfacial layer and conductive nitride passivation layer between high-k layer and top electrode in accordance with one embodiment.

FIG. 10. Schematic of a capacitor stack having a fluoride interfacial layer and metal oxide layer between high-k layer and top electrode in accordance with one embodiment.

FIG. 11. Process flow for deposition of capacitor stack in accordance with one embodiment.

DETAILED DESCRIPTION

Described herein are processes for passivating high-k film surfaces, for example, to enable electrode deposition from halide-based chemistry, particularly TiCl₄-based chemistry. Further described herein are methods to deposit TiN by ALD, CVD or pulsed CVD by using TiF₄ as a source chemical.

ALD type processes are used in some embodiments. ALD type processes are based on controlled, self-limiting surface reactions of precursor chemicals. Gas phase reactions are generally avoided by feeding the precursors alternately and sequentially into the reaction chamber. Vapor phase reactants are separated from each other in the reaction chamber, for example, by removing excess reactants and/or reactant byproducts from the reaction chamber between reactant pulses.

Briefly, a substrate is loaded into a reaction chamber and is heated to a suitable deposition temperature, generally at lowered pressure. Deposition temperatures are maintained below the thermal decomposition temperature of the reactants but at a high enough level to avoid condensation of reactants and to provide the activation energy for the desired surface reactions. Of course, the appropriate temperature window for any given ALD reaction will depend upon the surface termination and reactant species involved.

A first reactant is conducted or pulsed into the chamber in the form of a vapor phase pulse and contacted with the surface of the substrate. Conditions are preferably selected such that no more than about one monolayer of the first reactant is adsorbed on the substrate surface in a self-limiting manner. The appropriate pulsing times can be readily determined by the skilled artisan based on the particular circumstances. Excess first reactant and reaction byproducts, if any, are removed from the reaction chamber, for example by purging with an inert gas.

Purging the reaction chamber means that vapor phase precursors and/or vapor phase byproducts are removed from the reaction chamber such as by evacuating the chamber with a vacuum pump and/or by replacing the gas inside the reactor with an inert gas such as argon or nitrogen. Typical purging times are from about 0.05 to 20 seconds, more preferably between about 1 and 10, and still more preferably between about 1 and 2 seconds. However, other purge times can be utilized if necessary, when highly conformal step coverage over extremely high aspect ratio structures or other structures with complex surface morphology is needed.

A second gaseous reactant is pulsed into the chamber where it reacts with the first reactant bound to the surface. Excess second reactant and gaseous byproducts of the surface reaction, if any, are removed from the reaction chamber, preferably by purging with the aid of an inert gas and/or evacuation. The steps of pulsing and purging are repeated until a thin film of the desired thickness has been formed on the substrate, with each cycle leaving no more than a molecular monolayer. Additional steps comprising provision of a reactant and purging of the reaction space can be included to form more complicated materials, such as ternary materials.

As mentioned above, each pulse or phase of each cycle is preferably self-limiting. An excess of reactant precursors is supplied in each phase to saturate the susceptible structure surfaces. Surface saturation ensures reactant occupation of all available reactive sites (subject, for example, to physical size or “steric hindrance” restraints) and thus ensures excellent step coverage. Typically, less than one molecular layer of material is deposited with each cycle, however, in some embodiments more than one molecular layer is deposited during the cycle.

Removing excess reactants can include evacuating some of the contents of the reaction space and/or purging the reaction space with helium, nitrogen or another inert gas. In some embodiments purging can comprise turning off the flow of the reactive gas while continuing to flow an inert carrier gas to the reaction space.

The precursors employed in the ALD type processes may be solid, liquid or gaseous materials under standard conditions (room temperature and atmospheric pressure), provided that the precursors are in vapor phase before they are conducted into the reaction chamber and contacted with the substrate surface. “Pulsing” a vaporized precursor onto the substrate means that the precursor vapor is conducted into the chamber for a limited period of time. Typically, the pulsing time is from about 0.05 to 10 seconds. However, depending on the substrate type and its surface area, the pulsing time may be even higher than 10 seconds. Pulsing times can be on the order of minutes in some cases. The optimum pulsing time can be determined by the skilled artisan based on the particular circumstances.

The mass flow rate of the precursors can also be determined by the skilled artisan. In some embodiments the flow rate of metal precursors is preferably between about 1 and 1000 sccm without limitation, more preferably between about 100 and 500 sccm.

The pressure in the reaction chamber is typically from about 0.01 to about 20 mbar, more preferably from about 1 to about 10 mbar. However, in some cases the pressure will be higher or lower than this range, as can be determined by the skilled artisan given the particular circumstances.

Before starting the deposition of the film, the substrate is typically heated to a suitable growth temperature. The growth temperature varies depending on the type of thin film formed, physical properties of the precursors, etc. The growth temperatures are discussed in greater detail below in reference to each type of thin film formed. The growth temperature can be less than the crystallization temperature for the deposited materials such that an amorphous thin film is formed or it can be above the crystallization temperature such that a crystalline thin film is formed. The preferred deposition temperature may vary depending on a number of factors such as, and without limitation, the reactant precursors, the pressure, flow rate, the arrangement of the reactor, crystallization temperature of the deposited thin film, and the composition of the substrate including the nature of the material to be deposited on. The specific growth temperature may be selected by the skilled artisan.

Examples of suitable reactors that may be used include commercially available ALD equipment such as the F-120® reactor, Pulsar® reactor and Advance® 400 Series reactor, available from ASM America, Inc of Phoenix, Ariz. and ASM Europe B.V., Almere, Netherlands. In addition to these ALD reactors, many other kinds of reactors capable of ALD growth of thin films, including CVD reactors equipped with appropriate equipment and means for pulsing the precursors can be employed. Preferably, reactants are kept separate until reaching the reaction chamber, such that shared lines for the precursors are minimized. However, other arrangements are possible, such as the use of a pre-reaction chamber as described in U.S. application Ser. Nos. 10/929,348, filed Aug. 30, 2004 and 09/836,674, filed Apr. 16, 2001, the disclosures of which are incorporated herein by reference.

The growth processes can optionally be carried out in a reactor or reaction space connected to a cluster tool. In a cluster tool, because each reaction space is dedicated to one type of process, the temperature of the reaction space in each module can be kept constant, which improves the throughput compared to a reactor in which the substrate is heated up to the process temperature before each run.

The passivation process described herein can be carried out in the same reactor as prior and/or subsequent deposition processes. In some cases the passivation process can be performed in a different reactor either in same cluster tool or in a reactor located in different cluster tool.

Passivation of Oxide Film Surface

In some embodiments an oxide film surface is passivated. The oxide film can be formed by any methods known in the art. In some embodiments the oxide film is formed by CVD. In some embodiments, the oxide film is formed by ALD. In some embodiments the oxide surface is formed by oxidation.

In a typical ALD process for depositing thin films, one deposition cycle comprises exposing the substrate to a first precursor, removing unreacted first reactant and reaction byproducts from the reaction chamber, exposing the substrate to a second precursor, followed by a second removal step. Typically, halide precursors, such as TiCl₄, are used as precursors in ALD deposition because those precursors are inexpensive and relatively stable, but at the same time reactive towards different types of surface groups. H₂O and NH₃ are widely used for oxide and nitride deposition, respectively, as second precursors. Also metalorganic and organometallic precursors are used typically for ultra high k film depositions because suitable halide precursor do not exist for many of the metals, such as Sr and Ba, that are used in ultra high k films, such as SrTi_(x)O_(y), BaTi_(x)O_(y), Sr_(x)Ba_((1-x))Ti_(y)O, and SrBi_(x)Ta_(y)O_(z). Typical second precursors used in combination with metalorganic and organometallic first precursors are O₃, oxygen atoms, oxygen based plasmas, oxygen based radicals and water. Descriptions of ALD of ultra-high k films can be found, for example, in U.S. Pat. Nos. 7,108,747 and 20060219157, both of which are incorporated herein by reference.

Typical capacitor structures used in the semiconductor industry are metal-insulator-semiconductor (MIS) and metal-insulator-metal (MIM). Further types of capacitors include metal-insulator-metal-insulator-metal (MIMIM) and metal-insulator-metal-insulator-semiconductor (MIMIS). Memory capacitors and decoupling capacitors are just some of applications for capacitors in the semiconductor industry.

Titanium nitride is a widely used electrode material for capacitors in the semiconductor industry. It can be deposited by a number of different deposition processes, such as ALD, pulsed CVD or CVD. The typical and most useful precursor for TiN deposition is TiCl₄, primarily because it is a liquid with relatively high vapor pressure. A description of titanium nitride deposition can be found, for example, in U.S. patent application 20060060137, which is incorporated herein by reference.

However, the integration of SrTiO₃ and titanium chloride based metal electrode processes (CVD or ALD) in insulator-metal structures turned out to be challenging due to fundamental properties of the material. It was found that TiCl₄ based chemistry is not suitable for the top electrode deposition due to a severe reaction of the chloride based chemistry with the underlying SrTiO₃, leading to complete destruction of the insulator-metal interface and structure.

Titanium nitride electrodes have been successfully used in combination with ultra-high k films, such as SrTiO₃, but in these cases the titanium nitride top electrode has been deposited by physical vapor deposition (PVD) or only the bottom electrode has been deposited by ALD or CVD. Good results obtained by using TiN bottom electrodes and PVD platinum top electrodes on SrTiO₃ dielectric are described, for example in Menou, N., et al., 0.5 nm EOT Low Leakage ALD SrTiO ₃ on TiN MIM Capacitors for DRAM Applications IEDM 2008, San Francisco, USA. However, ALD or CVD deposition methods are preferred in top electrode deposition of the future devices because of less damage and more accurate control of thickness and uniformity and better step coverage.

In some embodiments the processes disclosed herein enable the use of chloride-based precursors, such as TiCl₄ based chemistry for depositing electrodes in ultra-high k film stacks such as MIM capacitor stacks.

The problem for depositing titanium nitride films from TiCl₄-based chemistry (or other Cl, I, or Br-based chemistry) on top of, for example, SrTiO₃ films is that TiCl₄ corrodes the dielectric and ruins the electrical properties of the capacitors. Corrosion possibly takes place because the solid phase of SrCl₂ will be formed during the electrode deposition from TiCl₄. This can be seen in FIG. 1a and FIG. 2.

At least some ultra-high-k materials comprising Sr and Ba, such as SrTiO₃, are susceptible to chloride, bromide, or iodide attack. TiCl₄ chemistry ruins the stack i.e. SrTiO₃ dielectric properties. Without being held to a theory, it is believed that it is likely due to the formation of solid SrCl₂, which is more stable at room temperature than SrO. Different halide chemistries were used for top electrode deposition (TiI₄, TiCl₄ and TiF₄). TiI₄ and TiCl₄ both adversely affected the properties of the dielectric material. Surprisingly, TiF₄ did not adversely affect the properties of the dielectric material. This was somewhat surprising because SrI₂ would be expected to be less stable than SrO (see the Table 1).

TABLE 1 Heat of formation Material (H °298 K) kJ/mol SrO −592.0 SrF2 −1217.1 SrCl2 −828.9 SrBr2 −718.0 SrI2 −561.5

Surprisingly TiF₄ worked despite the fact the SrF₂ is much more stable than SrO₂. In theory SrF₂ would be formed most favorably of the all the Sr halides. Since Cl, Br, I based chemistry ruins the SrTiO₃, one skilled in the art would expect that F based chemistry should also be problematic based on the energy of formation. However, it was surprising that TiF₄ didn't corrode the high-k dielectric layer. Without being bound to a particular theory we believe that TiF₄ forms an ultra-thin layer of SrF₂ which passivates the surface.

Chloride, bromide or iodide based chemistry described herein means that precursors contains at least one chlorine, bromine or iodine atom in the precursor molecule. In some cases, all of the ligands in the cases of metal chloride, bromide or iodide precursors are chlorine atoms, bromide atoms or iodine atoms, respectively. For example, in case of titanium halide TiX₄, where X is metal chloride, bromide or iodide, all four of the X's are either chlorides, bromides or iodides, preferably chlorides. Chloride, bromide or iodide based chemistries described herein may also use precursors which have organic ligands, but which have at least one chlorine, bromine or iodine atom in the precursor molecule.

In some embodiments the substrate surface is susceptible to chloride, bromide or iodide attack. Preferably the surface is sensitive or susceptible to chloride attack, such as TiCl₄ attack. The substrate surface that is susceptible to chloride, bromide or iodide attack is preferably a surface comprising a dielectric material, more preferably a surface comprising a material having higher dielectric constant than silicon dioxide and most preferably a material having Sr or Ba atoms, such as SrTi_(x)O_(y), BaTi_(x)O_(y), Sr_(x)Ba_((1-x))Ti_(y)O_(z) and SrBi_(x)Ta_(y)O_(z). Chloride, bromide, or iodide attack, as used herein, means that the chloride, bromide or iodide will change, degrade, or destroy the desired properties of the underlying substrate or film so that the properties are no longer as desirable and in some cases are no longer suitable for their intended use. Fluoride, on the other hand, may also react with the substrate surface but instead of degrading the desired properties of the underlying substrate or film it forms a passivating layer which may protect the underlying substrate or film from further chloride, bromide, or iodide attack in subsequent processing.

High-k films, such as SrTi_(x)O_(y), BaTi_(x)O_(y), Sr_(x)Ba_((1-x))Ti_(y)O_(z) and SrBi_(x)Ta_(y)O_(z), surfaces can be passivated and protected by using a fluoride containing chemical. High-k film surfaces are treated with a fluoride containing precursor in a suitable reactor, for example, in one of the ALD reactors listed above. The process is preferably a gas-phase process. Preferably the passivation is done by using one or more transition metal fluorides, such as TiF₄, TaF₅, NbF₅, WF_(x), MoF_(x), VF_(x). Most preferably the passivation is done using TiF₄. However, other fluoride containing chemicals can also be used such as NF₃, NH₄F, F₂, CF₄, SF₆, F-containing chemicals or plasmas and radicals of the mentioned chemicals or fluoride atoms. In other embodiments, volatile noble metal fluorides, such as RuF_(x) and IrF_(x) may be used.

In some embodiments the passivating layer is formed from high-k material through reaction of fluoride containing precursor with the surface of the substrate. Preferably the passivating layer is formed from a high-k film, more preferably it is formed from SrTi_(x)O_(y), BaTi_(x)O_(y), Sr_(x)Ba_((1-x))Ti_(y)O_(z) or SrBi_(x)Ta_(y)O_(z) layers. In some embodiments, the passivating layer is preferably not deposited on top of the substrate material, but rather is formed through an exchange reaction of fluoride containing precursor and the high-k material itself, which forms an ultra-thin fluoride passivating layer. However, in other embodiments a conductive metal nitride passivation layer may be deposited using the fluorine precursor, as described below. Many of the high-k materials from which the passivating layer will be formed, such as SrTi_(x)O_(y), BaTi_(x)O_(y), Sr_(x)Ba_((1-x))Ti_(y)O_(z) and SrBi_(x)Ta_(y)O_(z), have a perovskite type of structure, which have relatively low-k value in amorphous phase, but when crystallized, can have high k-values. In some embodiments the high-k material has a k value preferably in the range of about 50 to about 1000, more preferably from about 60 to about 500 and most preferably from about 70 to about 350. However, the calculated k-value for the high-k dielectric in the capacitor stack may be less or more depending on the material itself and the thickness of the high-k material.

In some embodiments the passivation layer is preferably between about 1 Å and 50 Å thick, even more preferably less than 20 Å thick, and most preferably less than about 15 Å thick.

The passivation treatment may be done with substrate temperatures from about 20 to about 500° C. depending on the fluoride chemical used. The pressure during the passivation treatment in the reaction chamber is typically from about 0.01 to about 20 mbar, more preferably from about 1 to about 10 mbar. However, in some cases the temperature and/or pressure will be higher or lower than this range, as can be determined by the skilled artisan given the particular circumstances. One pulse, preferably from about 0.05 to 120 seconds, more preferably between about 0.1 and 60, and still more preferably between about 1 and 30 seconds, of fluorine-based chemical is typically enough to passivate the surface, but in some cases other pulse times can be utilized if necessary, such as in case of batch reactors or where highly conformal step coverage over extremely high aspect ratio structures or other structures with complex surface morphology is needed.

In some embodiments the fluoride treatment or passivation can be performed at the same time as or right after the post-deposition anneal i.e. in-situ at the same tool as where the post deposition anneal is carried out.

In one embodiment the fluoride passivation layer is formed during an etch step after the dielectric deposition. Prior to the top electrode deposition step, the dielectric layer may be patterned and etched or etched without patterning. Using a fluorine containing chemical in the etching step can form the passivation layers.

In one embodiment the fluoride passivation layer is formed during an etch step after the top electrode deposition. The top electrode is patterned and etched or etched without patterning. Using fluorine containing chemical in the etching step forms the passivation layer in the high-k layer.

In one embodiment the fluoride surface is treated with a nitrogen containing chemical after the passivation treatment. Preferably the nitrogen containing chemical is selected from the group consisting of NH₃, N₂H₂, nitrogen containing plasma, radicals or atoms. Most preferably the nitrogen containing chemical is NH₃. The nitrogen containing chemical may also be selected from nitrogen containing chemicals, such as amino containing silanes, amino containing silazanes, amino containing germanes or amino containing boranes. By using TiF₄ as a passivation chemical and NH₃ as a nitrogen containing chemical a conductive TiN layer is formed on the top of the high-k dielectric layer. Deposition of conductive nitride layer, such as TiN, by using fluoride precursors, such as TiF₄, can be continued by following the examples of ALD or CVD nitrides by using fluoride precursors disclosed herein. Thus a conductive nitride passivation layer can be formed on top of the fluoride passivation layer. Preferably the thickness of the conductive nitride passivation layer made by using fluoride based chemistry is less than about 100 Å, more preferably less than 30 Å and most preferably less than 15 Å. Multiple ALD cycles (e.g. TiF₄ pulses/NH₃ pulses) can be used to deposit the layer to a desired thickness. For example, in some embodiments about 2 to about 10 ALD deposition cycles are performed. The skilled artisan will appreciate that the number of cycles can be selected based on the desired thickness of the deposited thin film.

In some embodiments, any type of layer typically used in the manufacture of integrated circuits can be deposited on top of the passivated surface.

In some embodiments a TiN electrode can be deposited on top of the passivated dielectric surface or on top of the conductive TiN layer made using TiF₄ based chemistry using TiCl₄ and NH₃. In some embodiments, the top electrode can be deposited by ALD (or CVD) using a precursor comprising fluorine as discussed below.

In some embodiments a metal oxide layer, such as a high-k dielectric layer, is deposited on top of the passivated layer. This metal oxide layer is deposited using a halide precursor, such as by using chloride, bromide or iodide based chemistry, preferably chloride based chemistry, by using any chemical deposition methods, such as ALD or CVD and variations of those. For example, HfO₂ could be deposited by ALD on top of the passivated oxide layer by using HfCl₄ and H₂O as precursors. Similarly ZrO₂ could be deposited by ALD on top of the passivated oxide layer by using ZrCl₄ and H₂O as precursors. There are many ALD and CVD deposition processes for metal oxides using metal chlorides, bromides or iodides as precursors and person skilled in the art can choose the right metal oxide process and right metal oxide material deposited on top of the passivated oxide layer depending on the particular application and its needs.

In some embodiments a semiconducting layer is deposited on top of the passivated oxide layer by using chloride based chemistry by using any chemical deposition methods, such as ALD or CVD.

Deposition on Top of the Passivated Surface by ALD or CVD

In some embodiments one or more films are deposited on top of the passivated dielectric surface or on top of the conductive TiN layer that were made using a fluorine containing compound.

Preferably, a film deposited on top of the passivated surface is deposited using a precursor comprising chlorine, bromine, or iodine. FIG. 5 is a schematic flow chart illustrating one method for forming a semiconductor structure on a substrate. In some embodiments a TiN film is deposited using TiCl₄ and NH₃ precursors by ALD or CVD

Deposition of ALD Nitrides by Using Fluoride Precursors

In some embodiments, the top electrode can be formed over the high-k dielectric using a compound comprising fluorine. In some embodiments the passivation layer is not formed separately from the top electrode because a compound comprising fluorine can be used to deposit the top electrode.

Any of the following precursors can be used in the various ALD nitride or carbon containing nitride processes disclosed herein. Other precursors will be apparent to the skilled artisan. In particular, precursors comprising transition metal fluorides are utilized.

In some embodiments the substrate surface is susceptible to chloride, bromide or iodide attack. Preferably the surface is sensitive or susceptible to chloride attack, such as TiCl₄ attack. The substrate surface that is susceptible to chloride, bromide or iodide attack is preferably a surface comprising a dielectric material, more preferably a surface comprising a material having higher dielectric constant than silicon dioxide and most preferably a material having Sr or Ba atoms, such as SrTi_(x)O_(y), BaTi_(x)O_(y), Sr_(x)Ba_((1-x))Ti_(y)O, and SrBi_(x)Ta_(y)O_(z). Chloride, bromide, or iodide attack, as used herein, means that the chloride, bromide or iodide will change, degrade, or destroy the desired properties of the underlying substrate or film so that the properties are no longer as desirable and in some cases are no longer suitable for their intended use. Fluoride, on the other hand, may also react with the substrate surface but instead of degrading the desired properties of the underlying substrate or film it forms a passivating layer which may protect the underlying substrate or film from further chloride, bromide, or iodide attack in subsequent processing.

In some embodiments, metal nitrides can be deposited using a fluoride precursor and a nitrogen precursor. In these embodiments passivation may not be done because a precursor comprising fluorine is used to deposit the metal nitride.

In some embodiments the fluoride precursors include volatile transition metal fluorides such as TiF₄, TaF₅, NbF₅, WF_(x), MoF_(x), VF_(x).

The second precursor for ALD deposition of a nitride film may include for example, NH₃, N₂H₂, nitrogen containing plasma, radicals or atoms, such as mixture of N₂/H₂ plasma, radicals or atoms. Preferably the nitrogen containing chemical is NH₃. Nitrogen containing chemical may also be selected from nitrogen containing chemicals, such as amino containing silanes, amino containing silazanes, amino containing germanes or amino containing boranes.

The ALD of nitrides by using fluoride precursors can done in temperatures from about 20 to about 700° C. depending on the fluoride chemical used. Preferably the deposition temperature is from about 250 to about 500° C. More preferably the deposition temperature is from about 300 to about 450° C. when using thermally activated nitrogen reactants as the second precursor, which does not contain nitrogen containing plasma, N-radicals or N-atoms. The pressure during the nitride deposition in the reaction chamber is typically from about 0.01 to about 20 mbar, more preferably from about 1 to about 10 mbar. However, in some cases the pressure will be higher or lower than this range, as can be determined by the skilled artisan given the particular circumstances. One pulse, preferably from about 0.05 to 20 seconds, more preferably between about 1 and 10, and still more preferably between about 1 and 2 seconds, of chemical is usually enough to passivate the surface, but in some cases other purge times can be utilized if necessary, such as in the case of batch reactors or where highly conformal step coverage over extremely high aspect ratio structures or other structures with complex surface morphology is needed.

In some embodiments, multiple ALD cycles can be used to deposit a nitride layer to a desired thickness. For example, in some embodiments about 2 to about 1000 ALD deposition cycles are performed. The skilled artisan will appreciate that the number of cycles can be selected based on the desired thickness of the deposited thin film.

In preferred embodiments TiN is deposited by ALD by using TiF₄ as a fluoride precursor and NH₃ as a nitrogen precursor. One example for this embodiment is described in example 1. TiF₄ is a solid at room temperature and pressure. The preferred source temperature range for TiF₄ is from about 100 to about 300° C., more preferably from about 150 to about 200° C. The preferred reaction temperature range for deposition is from about 250 to about 700° C., and more preferably from about 300 to about 450° C. When high work function is needed the deposition can be carried out with a reaction temperature range from about 250 to about 350° C.

In other preferred embodiments TiN is deposited by ALD by using TiF₄ as a fluoride precursor and mixture of N₂/H₂ plasma, radicals or atoms as a nitrogen precursor. Preferred source temperature range for TiF₄ is from about 100 to about 300° C., more preferably from about 150 to about 200° C. Preferred reaction temperatures ranges can be lower because of more reactive nitrogen precursors, thus making lower limits of the preferred reaction temperature range somewhat lower. For deposition using mixture of N₂/H₂ plasma, radicals or atoms as a nitrogen precursor the preferred reaction temperature is from about 100 to about 700° C., more preferably from about 200 to about 450° C.

In some embodiments the TiN film deposited using TiF₄ has a thickness of less than about 20 nm, preferably less than about 10 nm and more preferably less than about 5 nm and has a resistivity of less than about 1000 μΩcm, preferably less than about 750 μΩcm, more preferably less than about 500 μΩcm and most preferably less than about 400 μΩcm. It may be noted that in very thin films below 10 nm thick the thickness may increase the resistivity of the film.

In some embodiments the TiN film deposited using TiF₄ has fluorine as a desired impurity because fluorine can increase the work function. The TiN films deposited with TiF₄ can have a fluorine content preferably above 0.5 at-%, more preferably above 2 at-% and if desired even more than 5 at-% of fluorine can be incorporated into TiN films.

In yet another embodiment TaCN or NbCN can be deposited by ALD by using TaF₅ or NbF₅ as a fluoride precursor and hexamethyldisilazane (HMDS), tetramethyldisilazane (TMDS), and bisdiethylaminosilane (BDEAS) as a nitrogen precursors. Details of these process can be found from U.S. patent application 20080317955, which incorporated herein by reference. One example for this embodiment is described in example 2.

Yet another benefit of using the fluorine containing chemical in the metal electrode deposition step is the fluorine impurity left in the formed metal film. Fluorine is the most electronegative atom known and will increase the work function of the formed metal layer as demonstrated for example in ref. Appl. Phys. Lett. 96, 053506 (2010). Work function of the metal layer is one of the most important parameters that determine the leakage current density of a MIM capacitor and therefore a high work function of the metal layer is highly desirable. Work function of the metal gate also largely determines the threshold voltage in transistor applications and high work function materials are preferred for PMOS. Suitable work function range for PMOS is in the range of 5.0-5.2 eV. Metal gate applications and work function adjustment are also disclosed in U.S. Pat. Nos. 7,045,406 and 6,858,524, both of which incorporated herein by reference.

Deposition of Nitride by CVD or Pulsed CVD Using Fluoride Precursors

Any of the following precursors can be used in the various CVD nitride or carbon containing nitride processes disclosed herein. In particular, precursors comprising transition metal fluorides are disclosed. Description for pulsed CVD of titanium nitride deposition can be found, for example, in U.S. patent application 20060060137 and by replacing the metal precursor of U.S. patent application 20060060137 by fluoride precursor described herein, the pulsed CVD of any metal nitrides can be done in a similar manner.

In some embodiments the substrate surface is susceptible to chloride, bromide or iodide attack. Preferably the surface is sensitive or susceptible to chloride attack, such as TiCl₄ attack. The substrate surface that is susceptible to chloride, bromide or iodide attack is preferably a surface comprising a dielectric material, more preferably a surface comprising a material having higher dielectric constant than silicon dioxide and most preferably a material having Sr or Ba atoms, such as SrTi_(x)O_(y), BaTi_(x)O_(y), Sr_(x)Ba_((1-x))Ti_(y)O_(z) and SrBi_(x)Ta_(y)O_(z). Chloride, bromide, or iodide attack, as used herein, means that the chloride, bromide or iodide will change, degrade, or destroy the desired properties of the underlying substrate or film so that the properties are no longer as desirable and in some cases are no longer suitable for their intended use. Fluoride, on the other hand, may also react with the substrate surface but instead of degrading the desired properties of the underlying substrate or film it forms a passivating layer which may protect the underlying substrate or film from further chloride, bromide, or iodide attack in subsequent processing.

In some embodiments, metal nitrides can be deposited using a fluoride precursor and a nitrogen precursor. In these embodiments passivation may not be done because a precursor comprising fluorine is used to deposit the metal nitride.

In some embodiments the fluoride precursors include volatile transition metal fluorides such as, TiF₄, TaF₅, NbF₅, WF_(x), MoF_(x)VF_(x).

The second precursors for CVD deposition of a nitride film include, for example, NH₃, N₂H₂, nitrogen containing plasma, radicals or atoms, such as mixture of N₂/H₂ plasma, radicals or atoms. Preferably the nitrogen containing chemical is NH₃. Nitrogen containing chemical may also be selected from nitrogen containing chemicals, such as amino containing silanes, amino containing silazanes, amino containing germanes or amino containing boranes.

The CVD of nitrides by using fluoride precursor can be done in temperatures from about 20 to bout 700° C. depending on the fluoride chemical used. Preferably the deposition temperature is from about 250 to about 500° C. More preferably the deposition temperature is from about 300 to about 450° C. when using thermally activated nitrogen reactants as second precursor, which does not contain nitrogen containing plasma, N-radicals or N-atoms. In embodiments with nitrogen containing plasma, N-radicals or N-atoms, the preferred reaction temperature ranges are lower because of more reactive nitrogen precursors, thus making lower limits of the preferred reaction temperature range somewhat lower. For deposition using mixture of nitrogen containing plasma, N-radicals or N-atoms as a nitrogen precursor the preferred reaction temperature is from about 20 to about 700° C., more preferably from about 100 to about 450° C.

The pressure during the nitride deposition in the reaction chamber is typically from about 0.01 to about 20 mbar, more preferably from about 1 to about 10 mbar. However, in some cases the pressure will be higher or lower than this range, as can be determined by the skilled artisan given the particular circumstances. In case of pulsed CVD, the second precursor i.e. nitrogen containing precursor can be flowed in continuous manner in to the reaction chamber, while the fluoride chemical is introduced as a pulses in to the reaction chamber. In some cases of pulsed CVD, the both precursors can be flowed in pulses at the same time in to the reaction chamber. Pulses can be partially or totally overlapping each other. In case of CVD, both precursors can be flowed in continuous manner at the same time in to the reaction chamber.

In a preferred embodiment TiN is deposited by CVD or pulsed CVD by using TiF₄ as a titanium precursor and NH₃ as a nitrogen precursor. One example for this embodiment is described in example 3. Preferred source temperature range for TiF₄ is from about 100 to about 300° C., more preferably from about 150 to about 200° C. Preferred reaction temperature range for deposition is from about 250 to about 700° C., more preferably from about 300 to about 450° C.

In a yet another embodiment the TiN is deposited by pulsed CVD by using TiF₄ as a titanium precursor and NH₃ as a nitrogen precursor. In preferred embodiment the NH₃ pulse is longer than the TiF₄ pulse. In other embodiment the NH₃ flow to reactor is kept constant and TiF₄ pulses are introduced in reactor. In other embodiment the NH₃ flow is kept constant but decreased, preferably decreased of more than about 50%, more preferably of more than about 75%, during the TiF₄ pulse.

In other preferred embodiments TiN is deposited by CVD or pulsed CVD by using TiF₄ as a fluoride precursor and mixture of N₂/H₂ plasma, radicals or atoms as a nitrogen precursor. Preferred source temperature range for TiF₄ is from about 100 to about 300° C., more preferably from about 150 to about 200° C. Preferred reaction temperature ranges are lower because of more reactive nitrogen precursors, thus making the lower limits of the preferred reaction temperature range somewhat lower. For deposition using mixture of N₂/H₂ plasma, radicals or atoms as a nitrogen precursor the preferred reaction temperature is from about 100 to about 700° C., more preferably from about 200 to about 450° C.

In some embodiments the TiN film deposited using TiF₄ has a thickness of less than about 20 nm, preferably less than about 10 nm and more preferably less than about 5 nm and has a resistivity of less than about 1000 μΩcm, preferably less than about 500 μΩcm, more preferably less than about 300 μΩcm and most preferably less than about 200 μΩcm. It may be noted that in very thin films below 10 nm thick the thickness may increase the resistivity of the film.

In some embodiments the TiN film deposited using TiF₄ has fluorine as a desired impurity because fluorine can increase the work function. The TiN films deposited with TiF₄ can have a fluorine content preferably above 0.5 at-%, more preferably above 2 at-% and, if desired, even more than 5 at-% of fluorine can be incorporated into TiN films.

In yet another embodiment TaCN or NbCN is deposited by CVD or pulsed CVD by using TaF₅ or NbF₅ as a fluoride precursor and hexamethyldisilazane (HMDS), tetramethyldisilazane (TMDS), and bisdiethylaminosilane (BDEAS) as a nitrogen precursors or with other precursors described in US patent application 2008031795.

Yet another benefit of using the fluorine containing chemical in the metal electrode deposition step is the fluorine impurity left in the formed metal film. Fluorine is the most electronegative atom known and will increase the work function of the formed metal layer as demonstrated for example in ref. Appl. Phys. Lett. 96, 053506 (2010). Work function of the metal layer is one of the most important parameters that determine the leakage current density of a MIM capacitor and therefore a high work function of the metal layer is highly desirable. Work function of the metal gate also largely determines the threshold voltage in transistor applications and high work function materials are preferred for PMOS. Most desirable effective work function range for PMOS is in the range of 5.0-5.2 eV.

Work Function of the Materials Deposited by Using Fluorine Containing Chemicals

Preferably the work function of the material deposited using fluorine containing chemicals results to an effective work function of the gate or capacitor stack above 4.8 eV, more preferably above 4.9 eV and most preferably above 5.0 eV and optimum range being from about 5.0 eV to about 5.2 eV in metal gate applications in transistors. It may be preferably to have even higher work functions for capacitor applications, in which it might be preferred that work function is above 5.2 eV or in some case above 5.3 eV.

The use of high work function materials as an electrode in capacitor applications reduces the leakage current because it increases the energy barrier or conduction band offset for carrier/electron injection. The high work function is also preferable in capacitor applications where the dielectric is a material other than Ba or Sr containing dielectrics, for example, SrTi_(x)O_(y), BaTi_(x)O_(y), BaSr_(x)Ti_(y)O_(z), or SrBi_(x)Ta_(y)O_(z). The dielectric in capacitor applications can be for example a Zr or Hf based material, like ZrSiO_(x), HfSiO_(x), ZAZ (ZrO₂—Al₂O₃—ZrO₂ stack), ZrO₂, HfO₂.

In metal gate applications i.e. in transistor structures, in which the structure is metal-insulator-semiconductor (MIS), in cases where the high-k dielectric is not susceptible to chloride, bromide or iodide attack, it may be desirable to have a thin TiN layer made using precursors other than fluoride between the high-k layer and the TiN layer deposited using fluoride chemicals. This can be done for example, by using TiCl₄, TiBr₄, TiI₄ or metalorganic titanium compounds, The high-k dielectric in transistor applications can be, for example a Zr or Hf based material, like ZrSiO_(x), HfSiO_(x), ZAZ (ZrO₂—Al₂O₃—ZrO₂ stack), ZrO₂, HfO₂ or any other dielectric material. This way the properties of the gate stack can be tuned to optimum values by controlling the thickness of the thin TiN layer made using precursors other than fluoride containing precursors. Control of the thin TiN layer thickness made using precursors other than fluoride precursors (i.e. the lower TiN layer thickness) controls the effect of the fluorine on the work function of the whole gate stack. The thin TiN layer made by using precursors other than fluoride has preferably a thickness from about 2 to about 50 Å, more preferably from about 5 to about 30 Å and most preferably from about 10 to about 20 Å.

Process Flow for Deposition of High-k Capacitor Stack

Any of the following process flows or parts of the process flows or processes can be used in combination with the various ALD, CVD nitride or carbon containing nitride processes and fluoride treatment disclosed previously herein.

In one embodiment the previously described processes herein are used for making capacitor structures or parts of capacitors structures, preferably by utilizing silicon wafers, which have diameter of approximately from about 50 mm to about 675 mm, preferably having diameter approximately from about 100 mm to about 450 mm and most preferably having diameter approximately from about 200 mm to about 450 mm.

Process conditions and parameters for ALD, CVD nitride or carbon containing nitride processes and fluoride treatment that can be used are preferably the same as those disclosed previously.

In some embodiments the high-k material is susceptible to chloride, bromide or iodide attack. Preferably the surface is sensitive or susceptible to chloride attack, more preferably to TiCl₄ attack. A substrate surface that is susceptible to chloride, bromide or iodide attack is preferably a surface comprising a dielectric material, more preferably a surface comprising a material having higher dielectric constant than silicon dioxide and most preferably a material having Sr or Ba atoms, such as SrTi_(x)O_(y), BaTi_(x)O_(y), Sr_(x)Ba_((1-x))Ti_(y)O_(z) and SrBi_(x)Ta_(y)O_(z). Chloride, bromide, iodide attack or attack as used herein means that the chloride, bromide or iodide will attack the substrate surface and change, degrade, or destroy the desired properties of the underlying substrate or film so that the properties are no longer as desirable and in some cases are no longer suitable for their intended use. Fluoride may also react with the substrate surface but instead of changing the desired properties of the underlying substrate or film it forms a passivating layer which protects the underlying substrate or film from further chloride, bromide, or iodide attack.

Many of the high-k materials, such as SrTi_(x)O_(y), BaTi_(x)O_(y), Sr_(x)Ba_((1-x))Ti_(y)O_(z) and SrBi_(x)Ta_(y)O_(z), have a perovskite type of structure, which have relatively low-k value in amorphous phase, but when crystallized, can have high k-values, preferably in the range of about 50 to about 1000, more preferably from about 60 to about 500 and most preferably from about 70 to about 350. However, the calculated k-value for the high-k dielectric in the capacitor stack may be less or more depending on the material itself and the thickness of the high-k material. Post deposition anneal is usually performed for crystallization of these films. However, in some cases the high-k film may be totally or partially crystallized after deposition before post deposition anneal step, in which case post deposition anneal may not necessarily be needed, but can be performed in order to get better electrical properties for the films.

Post deposition anneal i.e. anneal performed in some step after high-k layer deposition, preferably in the next step after high-k deposition or in the next step after the top electrode deposition, most preferably in the next step after high-k deposition and before fluoride passivation, is preferably made at temperatures from about 300 to about 800° C., more preferably from about 400 to about 700° C. and most preferably from about 500 to about 650° C. The atmosphere for post-deposition anneal can, for example, comprise N₂, N₂/H₂ (forming gas), O₂, Ar, He. In some cases the fluoride treatment can be performed at the same time or just right after the post-deposition anneal i.e. in-situ at the same tool than where post deposition anneal is carried out.

In one embodiment the process flows or parts of process flow for making the structures described herein are as follows:

In one embodiment, a bottom electrode material is deposited with any deposition method, such as PVD, CVD or ALD. Preferably the bottom electrode is deposited by CVD or ALD. In some embodiments the material can be, for example, TiN, TaCN, NbCN, Pt, SrRuO₃, RuTiN or Ru. In some embodiments, the bottom electrode can be deposited also by using processes described herein

In some embodiments a high-k dielectric is then deposited that is susceptible to chloride, bromide, or iodide attack or that needs a passivation layer, such as Ba or Sr containing dielectric, like SrTi_(x)O_(y), BaTi_(x)O_(y), BaSr_(x)Ti_(y)O_(z), SrBi_(x)Ta_(y)O_(z), by using any method described herein. Preferably the high-k dielectric is deposited using ALD or CVD. The high-k dielectric may be deposited using Cp-compounds of Ba or Sr, for example as described in U.S. Pat. No. 7,108,747 and U.S. patent publication 20060219157. Methods for deposition of the high-k layer are described in also U.S. Pat. No. 7,108,747 and US patent application 20060219157. In some embodiments the high-k dielectric can be deposited using a compound comprising fluorine.

In some embodiments, after high-k deposition a post deposition anneal (PDA) can be done to crystallize the high-k. If it is not done right after high-k deposition, it can be done after top electrode deposition also. Preferably it is done at from about 300 to about 800° C., more preferably at from about 400 to about 700° C. and most preferably at from about 500 to about 650° C. The atmosphere for post-deposition anneal can, for example, comprise N₂, N₂/H₂ (forming gas), O₂, Ar, He. In some cases the fluoride treatment can be performed at the same or just right after the post-deposition anneal i.e. in-situ at the same tool than where post deposition anneal is carried out.

In some embodiments the high-k layer is passivated by a fluoride treatment. Preferably it is done by using a fluoride chemical that forms a passivation layer. Preferably by using transition metal fluorides, such as TiF₄, TaF₅, NbF₅, WF_(x), MoF_(x), VF_(x), and most preferably by using TiF₄. In some embodiments other fluoride containing chemicals can also be used such as NF₃, NH₄F, F₂, CF₄, SF₆, F-containing chemicals or plasmas and radicals of the mentioned chemicals or fluoride atoms. The fluoride precursor may also be chosen from volatile noble metal fluorides, such as RuF_(x) and IrF_(x). In some embodiments, HfF₄ and ZrF₄ can also be used.

In some embodiments one pulse of fluoride chemical is enough to form a passivation layer. In other embodiments a passivation layer film can be deposited, for example, by using the corresponding fluoride chemical, such as TiF₄, and a nitrogen chemical, such as NH₃ and by depositing many cycles as previously described herein. Yet in one embodiment, the passivation layer may be formed during an etch step done for the high-k layer, such as plasma etch step using fluorine containing chemical. The passivation layer film thickness is preferably less than about 100 Å, more preferably less than 30 Å and most preferably less than 15 Å

Next, the top electrode can be deposited by using TiCl₄ chemistry or other chemistry that would attack the high-k layer in the absence of a passivation layer. Preferably the top electrode is made by using TiCl₄ based chemistry using CVD or ALD. More preferably the process is pulsed CVD or ALD as described, for example, in US patent application 2006006013. In some embodiments the top electrode can be deposited using any of the compounds comprising fluorine disclosed herein.

If the top electrode is deposited with a method that does not corrode the underlying high-k layer, the fluoride passivation can be optionally done after the top electrode deposition step. After the top electrode deposition step, an etch step using a fluorine containing chemical is used to pattern the MIM stack. The fluoride passivation of the high-k layer is formed during the etch step. Passivation after formation of the top electrode can protect the high-k layer against undesirable reactions with subsequent processing materials, for example from undesirable reactions with the sidewalls of the high-k material.

Some parts of process flows are described in examples 4-7. Generalized process flow in one embodiment is described in FIG. 5.

The process flow described can be used as it is described or only parts of it can be used for deposition of capacitor structures. A person skilled in the art can make the right choices for correct process flow or parts of process flows for a particular type of capacitor structure of interest. For example, in some cases, if desired it is possible to deposit the passivation layer film between the bottom electrode and high-k material from a transition metal fluoride and nitrogen containing chemical, preferably from TiF₄ and NH₃, using the processes described herein.

Further, the passivation process described herein can be used also for other surfaces or process flows, not just for making MIM stacks and the other structures disclosed herein.

Structure of High-k capacitor Stack

The processes described herein can be used for depositing a capacitor stack having a layer comprising fluorine or fluoride interfacial layer 40 between the high-k layer 30 and electrode layer, preferably between the high-k layer 30 and top electrode layer 21 as shown in FIG. 6. In some embodiments, the layer comprising fluorine can also comprise material from the high-k or a metal from the overlying top electrode. The layer comprising fluorine 40 can also be between the bottom electrode 20 and high-k layer 30 as shown in FIG. 7 or both between the bottom electrode 21 and high-k layer 30 and top electrode 21 and high-k layer 30 as shown in FIG. 8. A conductive nitride passivation layer 41 can be on top of the layer comprising fluorine 40 as shown in FIG. 9. Preferably the thickness of the conductive nitride passivation layer 41 is less than about 100 Å, more preferably less than 30 Å and most preferably less than 15 Å. Further a metal oxide layer 31 can be on top of the fluoride passivation layer as shown in FIG. 10. The capacitor stack is preferably deposited on silicon wafer 10.

The thickness of the layer comprising fluorine 40 is preferably between about 1 Å to about 50 Å, more preferably about 2 Å to about 20 Å and most preferably about 3 Å to about 15 Å. One skilled in the art will realize that ultrathin films, such as 1-3 Å thick films, may not be continuous and thus may not be understood as a film. However, here the word film is used because of simplicity.

High-k dielectric film 49 preferably comprises, but is not limited, SrTi_(x)O_(y), BaTi_(x)O_(y), Sr_(x)Ba_((1-x))Ti_(y)O_(z), and SrBi_(x)Ta_(y)O_(z) or mixtures thereof, and have a perovskite type of crystalline structure.

Bottom electrode layer 20 comprises preferably Si, SiGe, TiN, TaCN, NbCN, Pt, SrRuO₃, RuTiN or Ru. Bottom electrode layer thickness is preferably from about 1 to about 50 nm, more preferably from about 3 to about 30 nm, most preferably about 5 to about 20 nm.

Top electrode layer 21 comprises preferably TiN, TaCN, NbCN, Pt, SrRuO₃, RuTiN or Ru. Top electrode layer thickness is preferably from about 1 to about 50 nm, more preferably from about 3 to about 30 nm, most preferably about 5 to about 20 nm.

Capacitor stack may comprise a non-planar structure such as three-dimensional structures comprising trenches, pores and stacked films.

Although the structures of stacks described herein are disclosed in the context of capacitor stacks, one skilled in the art can utilize the embodiments described herein other types of structures, such transistor structures, like NMOS and PMOS structures.

EXAMPLE 1

ALD TiN film was deposited on both silicon dioxide and SrTiO₃ substrates at a reaction temperature of 395° C. by using TiF₄ and NH₃ as a reactants. Source temperature for TiF₄ was 170° C. Pulse time for TiF₄ was 6 seconds and purge time 5 seconds. NH₃ pulse time was 2 seconds and purge time 10 s.

No damage or corrosion was observed when depositing ALD TiN film by using TiF₄ and NH₃ as a reactants, for example, on SrTiO₃ surfaces. Deposition of TiN can be continued by using TiCl₄ based chemistry also without damage or corrosion of SrTiO₃.

COMPARATIVE EXAMPLE 1

ALD TiN films were deposited on SrTiO₃ substrates at using TiI₄ and NH₃ as reactants. TiN films were also deposited on SrTiO₃ substrates using TiCl₄ and NH₃ as reactants. The ALD processes using TiCl₄ and TiI₄ both resulted in damage and corrosion to the SrTiO₃ surfaces. See FIGS. 1a and 2.

EXAMPLE 2

TaCN was deposited on top of SrTiO₃ films on 200 and 300 mm silicon wafers in a batch ALD reactor at 400° C. by using TaF₅ and tetramethyldisilazane (TMDS), a process described in US patent application 20080317955. No damage to the SrTiO₃ film was observed.

Analogously NbCN was deposited by using NbF₅ as a replacement for TaF₅ and no damage to the SrTiO₃ film was observed

Deposition of TiN can likely be continued using TiCl₄ based chemistry without damage or corrosion of SrTiO₃, if desired.

EXAMPLE 3

CVD TiN film can be deposited at reaction temperatures of 400-600° C. by using TiF₄ and NH₃ as a reactants. Source temperature for TiF₄ can be from about 170 to about 200° C. Continuous flow of NH₃ in the range of about 50 sccm to about 5000 sccm is introduced in to the reaction chamber. TiF₄ is introduced into reaction chamber in continuous manner or preferably in pulses, while flowing NH₃ continuously also into reaction chamber.

No damage or corrosion to the high-k material is likely to occur when depositing CVD TiN film by using TiF₄ and NH₃ as a reactants, for example, on SrTiO₃ surfaces. Deposition of TiN can be continued by using TiCl₄ based chemistry also without damage or corrosion of SrTiO₃.

EXAMPLE 4

ALD SrTiO₃ was deposited in ASM Pulsar® 2000 reactor at 250° C. (1,2,4-tertiarybutyl-Cp)₂Sr was used as the Sr precursor, heated to a temperature of 170° C. Ti(OMe)₄ was used as the Ti precursor, heated to a temperature of 145° C. H₂O at room temperature, 21° C. was used as the oxidizer. The ALD deposition was done by sequentially pulsing the precursors in the reactor in the following way: x.[(1,2,4-tertiarybutyl-Cp)₂Sr pulse, (1,2,4-tertiarybutyl-Cp)₂Sr purge, H₂O pulse, H₂O purge], y.[Ti(OMe)₄ pulse, Ti(OMe)₄ purge, H₂O pulse, H₂O purge]. x=2 and y=1 was used, leading to slightly Sr rich films. Pulse and purge times were as follows: (1,2,4-tertiarybutyl-Cp)₂Sr pulse 5 s, (1,2,4-tertiarybutyl-Cp)₂Sr purge 10 s, H₂O pulse 0.5 s, H₂O purge 5 s, Ti(OMe)₄ pulse 4 s, Ti(OMe)₄ purge 10 s, H₂O pulse 0.5 s, H₂O purge 5 s.

The pulsing sequence was repeated 175 times, which resulted in SrTiO₃ film with an average thickness of approximately 30 nm.

Then the SrTiO₃ film, deposited in the way explained in the previous paragraph, was transported to another ASM Pulsar® 2000 reactor and the ALD TiN top electrode was deposited on it at 395° C. The top electrode was deposited in the following way: 6 s TiF₄ (kept at 170° C.) pulse was introduced to the reactor, then a 5 s purge, then a 2 s NH₃ pulse, and then a 10 s purge. After this, ALD TiN was deposited at 395° C. by cycling 500 times TiCl₄+NH₃. TiCl₄ and NH₃ were at room temperature, 21° C. The pulse and purge times were: TiCl₄ pulse 0.1 s, TiCl₄ purge 3 s, NH₃ pulse 2 s, NH₃ purge 4 s. FIG. 1(b) shows a photograph of the wafer and FIG. 2 shows the sheet resistance of the TiN top electrode.

EXAMPLE 5

ALD SrTiO₃ was deposited in ASM Pulsar® 2000 reactor at 250° C. (1,2,4-tertiarybutyl-Cp)₂Sr was used as the Sr precursor, heated to a temperature of 170° C. Ti(OMe)₄ was used as the Ti precursor, heated to a temperature of 145° C. H₂O at room temperature, 21° C. was used as the oxidizer. The ALD deposition was done by sequentially pulsing the precursors in the reactor in the following way: x.[(1,2,4-tertiarybutyl-Cp)₂Sr pulse, (1,2,4-tertiarybutyl-Cp)₂Sr purge, H₂O pulse, H₂O purge], y.[Ti(OMe)₄ pulse, Ti(OMe)₄ purge, H₂O pulse, H₂O purge]. x=2 and y=1 was used, leading to slightly Sr rich films. Pulse and purge times were as follows: (1,2,4-tertiarybutyl-Cp)₂Sr pulse 5 s, (1,2,4-tertiarybutyl-Cp)₂Sr purge 10 s, H₂O pulse 0.5 s, H₂O purge 5 s, Ti(OMe)₄ pulse 4 s, Ti(OMe)₄ purge 10 s, H₂O pulse 0.5 s, H₂O purge 5 s.

The pulsing sequence was repeated 175 times, which resulted in SrTiO₃ film with an average thickness of approximately 30 nm.

Then the SrTiO₃ film, deposited in the way explained in the previous paragraph, was transported to another ASM Pulsar® 2000 reactor and the ALD TiN top electrode was deposited on it at 395° C. The top electrode was deposited in the following way: 1 s WF₆ (kept at room temperature, 21° C.) pulse was introduced to the reactor, then a 3 s purge. After this, ALD TiN was deposited at 395° C. by cycling 500 times TiCl₄+NH₃. TiCl₄ and NH₃ were at room temperature, 21° C. The pulse and purge times were: TiCl₄ pulse 0.1 s, TiCl₄ purge 3 s, NH₃ pulse 2 s, NH₃ purge 4 s. FIG. 3(a) shows a photograph of the wafer.

EXAMPLE 6

ALD SrTiO₃ was deposited in ASM Pulsar® 2000 reactor at 250° C. (1,2,4-tertiarybutyl-Cp)₂Sr was used as the Sr precursor, heated to a temperature of 170° C. Ti(OMe)₄ was used as the Ti precursor, heated to a temperature of 145° C. H₂O at room temperature, 21° C. was used as the oxidizer. The ALD deposition was done by sequentially pulsing the precursors in the reactor in the following way: x.[(1,2,4-tertiarybutyl-Cp)₂Sr pulse, (1,2,4-tertiarybutyl-Cp)₂Sr purge, H₂O pulse, H₂O purge], y.[Ti(OMe)₄ pulse, Ti(OMe)₄ purge, H₂O pulse, H₂O purge]. Pulse and purge times were as follows: (1,2,4-tertiarybutyl-Cp)₂Sr pulse 5 s, (1,2,4-tertiarybutyl-Cp)₂Sr purge 10 s, H₂O pulse 0.5 s, H₂O purge 5 s, Ti(OMe)₄ pulse 4 s, Ti(OMe)₄ purge 10 s, H₂O pulse 0.5 s, H₂O purge 5 s.

The pulsing sequence was repeated 175 times, which resulted in SrTiO₃ film with an average thickness of approximately 30 nm.

Then the SrTiO₃ film, deposited in the way explained in the previous paragraph, was transported to another ASM Pulsar® 2000 reactor and the ALD TiN top electrode was deposited on it at 395° C. The top electrode was deposited in the following way: 1 s WF₆ (kept at room temperature, 21° C.) pulse was introduced to the reactor, then a 3 s purge, then a 2 s NH₃ pulse, and then a 10 s purge. After this, ALD TiN was deposited at 395° C. by cycling 500 times TiCl₄+NH₃. TiCl₄ and NH₃ were at room temperature, 21° C. The pulse and purge times were: TiCl₄ pulse 0.1 s, TiCl₄ purge 3 s, NH₃ pulse 2 s, NH₃ purge 4 s. FIG. 4 (b) shows a photograph of the wafer.

EXAMPLE 7

ALD SrTiO₃ was deposited in ASM Pulsar® 2000 reactor at 250° C. (1,2,4-tertiarybutyl-Cp)₂Sr was used as the Sr precursor, heated to a temperature of 170° C. Ti(OMe)₄ was used as the Ti precursor, heated to a temperature of 145° C. H₂O at room temperature, 21° C. was used as the oxidizer. The ALD deposition was done by sequentially pulsing the precursors in the reactor in the following way: x.[(1,2,4-tertiarybutyl-Cp)₂Sr pulse, (1,2,4-tertiarybutyl-Cp)₂Sr purge, H₂O pulse, H₂O purge], y.[Ti(OMe)₄ pulse, Ti(OMe)₄ purge, H₂O pulse, H₂O purge]. Pulse and purge times were as follows: (1,2,4-tertiarybutyl-Cp)₂Sr pulse 5 s, (1,2,4-tertiarybutyl-Cp)₂Sr purge 10 s, H₂O pulse 0.5 s, H₂O purge 5 s, Ti(OMe)₄ pulse 4 s, Ti(OMe)₄ purge 10 s, H₂O pulse 0.5 s, H₂O purge 5 s.

The pulsing sequence was repeated 175 times, which resulted in SrTiO₃ film with an average thickness of approximately 30 nm.

Then the SrTiO₃ film, deposited in the way explained in the previous paragraph, was transported to another ASM Pulsar® 2000 reactor and the ALD TiN top electrode was deposited on it at 395° C. ALD TiN was deposited at 395° C. by cycling 500 times TiF₄+NH₃. TiF₄ was kept at 170° C. and NH₃ was at room temperature, 21° C. The pulse and purge times were: TiF₄ pulse 6 s, TiF₄ purge 5 s, NH₃ pulse 2 s, NH₃ purge 10 s. FIG. 4 shows a photograph of the wafer.

EXAMPLE 8

SrTiO₃ film is deposited on a substrate by any method, preferably by ALD or CVD. SrTiO₃ is either in amorphous phase or in the perovskite phase as deposited, or optionally is crystallized by a post deposition anneal treatment, (PDA). Then the SrTiO₃ film is exposed to a fluoride containing precursor, for example, TiF₄, TaF₅, NbF₅, WF_(x), MoF_(x) or VF_(x). Most preferably the passivation is done by using TiF₄. However, other fluoride containing chemicals can also be used such as NF₃, NH₄F, F₂, CF₄, SF₆, F-containing chemicals or plasmas and radicals of the mentioned chemicals or fluoride atoms. In other embodiments, the fluoride precursor include volatile noble metal fluorides, such as RuF_(x) and IrF_(x). Then the top electrode is deposited on the passivated SrTiO₃ by ALD technique, using chloride, bromide or iodide containing precursor, preferably by using TiCl₄.

EXAMPLE 9

SrTiO₃ film is deposited on a substrate by any method, preferably by ALD or CVD. SrTiO₃ is either in amorphous phase or in the perovskite phase as deposited, or optionally is crystallized by a post deposition anneal treatment, (PDA). Then the SrTiO₃ film is exposed to a fluoride containing precursor, for TiF₄, TaF₅, NbF₅, WF_(x), MoF_(x) or VF_(x). Most preferably the passivation is done by using TiF₄. However, other fluoride containing chemicals can also be used such as NF₃, NH₄F, F₂, CF₄, SF₆, F-containing chemicals or plasmas and radicals of the mentioned chemicals or fluoride atoms. In other embodiments, the fluoride precursor include volatile noble metal fluorides, such as RuF_(x) and IrF_(x). Then the top electrode is deposited on the passivated SrTiO₃ by CVD or pulsed CVD technique, using chloride, bromide or iodide containing precursor, preferably by using TiCl₄.

EXAMPLE 10

A SrTiO₃ film is deposited on a substrate by any method, preferably by ALD or CVD. SrTiO₃ is either in amorphous phase or in the perovskite phase as deposited, or optionally is crystallized by a post deposition anneal treatment, (PDA). Then the SrTiO₃ film is exposed to an etching step using fluorine containing precursor, for example NF₃, NH₄F, F₂, CF₄, SF₆, F-containing chemicals or plasmas and radicals of the mentioned chemicals or fluoride atoms. Then the top electrode is deposited on the passivated SrTiO₃ by ALD technique, using chloride, bromide or iodide containing precursor, preferably by using TiCl₄.

EXAMPLE 11

A SrTiO₃ film is deposited on a substrate by any method, preferably by ALD or CVD. SrTiO₃ is either in amorphous phase or in the perovskite phase as deposited, or optionally is crystallized by a post deposition anneal treatment, (PDA). Then a top electrode is deposited on the SrTiO₃ layer by a method that does not destroy the underlying SrTiO₃ layer, for example by PVD, or by ALD or CVD using metalorganic precursors. Then the top electrode is patterned and etched with fluorine containing chemical forming a fluoride passivation layer in the SrTiO₃ film.

EXAMPLE 12

TiN was deposited on Si/HfO₂ substrates with TiF₄+NH₃ chemistry at various temperatures, 300° C., 350° C. and 425° C. After depositions the effective work functions of the formed TiN layers were measured and found to be 5.25 eV (300° C.), 5.25 eV (350° C.), 4.97 eV (425° C.).

It will be appreciated by those skilled in the art that various modifications and changes can be made without departing from the scope of the invention. Similar other modifications and changes are intended to fall within the scope of the invention, as defined by the appended claims. 

We claim:
 1. A process for forming a titanium nitride containing thin film on a substrate comprising a high-k surface in a reaction chamber, the process comprising: depositing a first titanium nitride layer by at least one deposition cycle comprising: providing titanium fluoride into the reaction chamber in a vapor phase to contact the substrate comprising a high-k surface; and providing nitrogen containing vapor phase reactant to the reaction chamber such that the nitrogen containing vapor phase reactant reacts with the titanium fluoride to form a first titanium nitride layer; wherein the nitrogen containing vapor phase reactant comprises NH₃ or N-containing plasma and wherein the formed first titanium nitride layer comprises greater than 0.5 at-% F, and subsequently depositing a second titanium nitride layer over the formed first titanium nitride layer, wherein the second titanium nitride layer is deposited using a titanium precursor comprising chlorine, bromine or iodine, thereby forming the titanium nitride thin film.
 2. The process of claim 1, wherein the process for depositing the first titanium nitride layer is an atomic layer deposition (ALD) process.
 3. The process of claim 1, wherein the process for depositing the first titanium nitride layer is a chemical vapor deposition (CVD) or a pulsed CVD process.
 4. The process of claim 1, wherein the formed titanium nitride thin film has a work function above about 5.0 eV.
 5. The process of claim 1, wherein the formed titanium nitride thin film has a work function above about 5.2 eV.
 6. The process of claim 1, wherein the substrate is susceptible to chloride, bromide, or iodide attack.
 7. The process of claim 1, wherein the high-k surface comprises hafnium or zirconium.
 8. The process of claim 1, wherein the first titanium nitride layer serves as a passivation layer.
 9. The process of claim 1, wherein the first titanium nitride layer comprises greater than 2 at-% F.
 10. The process of claim 1, wherein the first titanium nitride layer comprises greater than 5 at-% F. 